Cutting tool made of A12O3-coated cBN-based sintered material

ABSTRACT

A cutting tool according to the present invention is coated with one or more Al 2 O 3  layers on at least a part of the surface of a cBN-based sintered material substrate taking part in cutting. The sintered material substrate is made of cBN in an amount of from 20% to 99% by volume and Al 2 O 3  having an average crystalline particle diameter of not more than 1 μm in an amount of from not less than 1.0% to less than 10% by volume. The Al 2 O 3  layer has a thickness (d) of from 0.5 μm to 50 μm. The average crystalline particle diameter (s) of Al 2 O 3  is from 0.01 μm to 4 μm if the thickness (d) of the Al 2 O 3  layer is from 0.5 μm to 25 μm or from not less than 0.01 μm to not more than 10 μm if the thickness (d) of the Al 2 O 3  layer is from more than 25 μm to 50 μm.

BACKGROUND OF THE INVENTION

1. Field of the Invention

The present invention relates to a cutting tool made of a cubic boron nitride (cBN) sintered material substrate coated with Al₂O₃. More particularly, the present invention relates to a cutting tool made of Al₂O₃-coated cBN-based sintered material having improved wear resistance and breakage resistance.

2. Description of the Related Art

Al₂O₃ is a material optimum for cutting iron-based materials because of its excellent chemical stability and hardness. However, Al₂O₃exhibits a poor toughness. Therefore, a cutting tool mainly composed of Al₂O₃ has a deteriorated stability against tool failure to disadvantage. In order to overcome this difficulty, a cutting tool consisting of a cemented carbide substrate having a relatively excellent toughness coated with Al₂O₃ has been commercialized.

In recent years, there is a growing need for high speed and efficiency and dry cutting in response to the trends of environment-friendly production. In the conventional tools, however, the cemented carbide substrate deforms excessively plastically at high cutting temperature, resulting in that the coating layer easily peels off or is destroyed.

As a means for solution to the problems, a method for coating a cBN-based sintered material excellent in high temperature hardness with Al₂O₃ has been proposed in JP-A-59-8679 (The term “JP-A” as used herein means an “unexamined published Japanese patent application”). However, since the adhesion between cBN-based sintered material and Al₂O₃ coating layer is insufficient and the optimization of the crystallinity of Al₂O₃ is insufficient, a remarkable enhancement of wear resistance and breakage resistance is not exhibited in cutting of hard materials such as hardened steel or high speed and efficiency cutting of steel.

SUMMARY OF THE INVENTION

It is an object of the present invention to provide a cutting tool which exhibits an excellent flank wear resistance and crater wear resistance particularly in cutting of high hardness difficult-to-cut ferrous materials or high speed and efficiency cutting of steel.

A cutting tool according to the present invention is coated with one or more Al₂O₃ layers on at least a part of the surface of a cBN-based sintered material substrate taking part in cutting. The sintered material substrate comprises cBN in an amount of 20% to 99% by volume and Al₂O₃ having an average crystalline particle diameter of not more than 1 μm in an amount of not less than 1.0% to less than 10% by volume. The Al₂O₃ layer has a thickness (d) of 0.5 μm to 50 μm . The average crystalline particle diameter (s) of Al₂O₃ is from 0.01 μm to 4 μm if the thickness (d) of the Al₂O₃ layer is from 0.5 μm to 25 μm (0.5 μm≦d≦25 μm ), and that of Al₂O₃ is from 0.01 μm to 10 μm if the thickness (d) of the Al₂O₃ layer is from more than 25 μm to 50 μm (25 μm<d≦50 μm ).

The incorporation of a proper amount of Al₂O, in a cBN-based sintered material substrate makes it possible to increase the adhesion of the Al₂O₃ layer or interlayer made of TiC_(x)N_(y)O_(Z) having an excellent bonding power with Al₂O₃, thereby enhancing the cutting properties. A particularly preferred content of Al₂O₃ is form 3.0% to less than 5.0%. The reason why the adhesion of the Al₂O₃ layer or interlayer can be thus increased is presumably as follows:

(1) Al₂O₃ constituting the coating layer and TiC_(x)N_(y)O_(Z) _(—) undergo nucleation with Al₂O₃ contained in cBN-based sintered material substrate as a starting point; and.

(2) the incorporation of Al₂O₃ in cBN-based sintered material substrate causes the residual stress characteristic to cBN-based sintered material substrate to change, thereby relaxing misfit of coating layer to residual stress (thermal stress, internal stress).

The homogeneous incorporation of fine Al₂O₃ particles having a particle diameter of not more than 1 μm in cBN-based sintered material substrate makes it possible to accelerate the formation of fine homogenous nuclei during the formation of Al₂O₃ or TiC_(x)N_(y)O_(Z) _(—) layer and hence form an Al₂O₃ layer having an excellent crystallinity and adhesion. If the content of Al₂O₃ falls below 1.0% by volume, it causes uneven nucleation during the formation of coating layer, thereby exerting an insufficient effect. On the contrary, if the content of Al₂O₃ exceeds 10% by volume, the mechanical properties inherent to Al₂O₃ is presumably reflected in the mechanical properties of cBN-based sintered material, thereby drastically deteriorating the breakage resistance of cBN-based sintered material substrate.

The Al₂O₃ layer is preferably mainly composed of α-Al₂O₃. The coating of cBN-based sintered material substrate with α-Al₂O₃ with a good adhesion makes it possible to inhibit wear on relieve face and crater wear and hence drastically prolong the life of tool. The coating of cBN-based sintered material substrate with κ-Al₂O₃ with a good adhesion, too, makes it possible to inhibit crater wear and prolong the life of tool. However, wear on relieve face can be little inhibited.

Further, the Al₂O₃ layer can be oriented on (012), (104), (110), (113), (024) or (116) plane with an orientation index of not less than 1.0 to form a coating layer excellent in wear resistance and strength. This orientation index can be defined by the following equation. The method for determining orientation index is described also in WO96/15286 (PCT/SE95/01347), etc.

TC(hkl)=I(hkl)/Io(hkl)×[(l/n)Σ{(hkl)/Io(hkl)}]⁻¹ where I(hkl): Intensity of (hkl) diffraction ray in XRD;

Io(hkl): Diffraction intensity in ASTM card of XRD; and

n: Number of diffraction rays used in calculation ((hkl) diffraction rays used are (012),(104),(110),(113),(024) and (116))

In the foregoing cutting tool, the Al₂O₃ layer may be complexed with the TiC_(x)N_(y)O_(Z) _(—) layer to form a laminate. Specific examples of the composite structure include (1) structure comprising an interlayer made of TiC_(x)N_(y)O_(Z) _(—) formed on the interface of Al₂O₃ layer with cBN-based sintered material substrate, (2) structure comprising a TiC_(x)N_(y)O_(Z) layer provided interposed between a plurality of Al₂O₃ layers, and (3) structure comprising a TiC_(x)N_(y)O_(Z) _(—) layer provided as an outermost layer.

Referring to the reason why the thickness of the Al₂O₃ layer is defined to a range of from 0.5 μm to 50 μm , if the thickness of the Al₂O₃ layer falls below the lower limit, the resulting coating effect is insufficient. On the contrary, if the thickness of the Al₂O₃ layer exceeds the upper limit, the coating layer is more liable to peeling, chipping or breakage. The thickness of the Al₂O₃ layer is preferably from about 3 to 40 μm. In particular, if the thickness of the Al₂O₃ layer is not more than 25 μm and the average crystal particle diameter (s) of Al₂O₃ is from 0.01 μm to 4 μm, the resulting product is excellent in flank wear resistance. If the thickness of the Al₂O₃ layer is more than 25 μm and the average crystal particle diameter (s) of Al₂O₃ is from 0.01 μm to 10 μm. the resulting product is excellent in crater wear resistance. If there are a plurality of Al₂O₃ layers, the total thickness of these Al₂O₃ layers is used to see whether the thickness of the Al₂O₃ layer is not more than 25 μm.

The formation of the foregoing Al₂O₃ layer or TiC_(x)N_(y)O_(Z) _(—) layer can be accomplished by CVD method such as thermal CVD method, plasma CVD method and moderate temperature CVD method or PVD method such as sputtering method and ion plating method.

On the other hand, the sintered material substrate is composed of cBN and a binder phase. If the content of cBN is not less than 20% by volume, the production of a thick binder phase which forms a mechanically weak point can be inhibited. The binder phase is preferably made of at least one of nitride, carbide and boride of metals belonging to the groups 4a, 5a and 6a in the periodic table and mutual solid-solution thereof as a main component besides Al₂O₃. The binder phase may further contains at least one of Al and Si incorporated therein. For the preparation of the sintered material substrate, a plasma sintering apparatus, hot press, ultrahigh pressure sintering apparatus, etc. may be used.

Since the cutting tool according to the present invention is made of a cBN-based sintered material substrate mainly composed of cBN having a hardness next to diamond, it exhibits an excellent plastic deformation resistance. Further, the coating with α-Al₂O₃, which is chemically stable, having a controlled structure makes it possible to improve crater resistance without causing chipping or peeling. Accordingly, the cutting tool according to the present invention exhibits a prolonged life in cutting of high hardness materials such as hardened steel or high speed and efficiency cutting of steel, which is impossible with existing tools due to the rise in cutting temperature.

DETAILED DESCRIPTION OF THE INVENTION

The present invention will be described in detail referring to the following specific examples.

EXAMPLE 1

cBN-based sintered material substrates shaped according to SNGN120408 (ISO Specification) having different formulations set forth in Table 1 were prepared. Subsequently, these cBN-based sintered material substrates were each coated with Al₂O₃ by an ordinary CVD method under the conditions set forth in Table 2 (Condition 1) and Table 3 (Condition 2). In some of these inserts, a TiC_(0.5)N_(0.5) layer is provided by an ordinary CVD method as an interlayer between the cBN-based sintered material substrate and the Al₂O₃ layer.

TABLE 1 Particle size (μm) Composition (vol-%) No. cBN Al₂O₃ Others Al₂O₃ A ≦8 <1 cBN: 45; TiN: 30; TiB₂: 5; AlN: 5; 0   impurities such as W and Co: 15 B ≦8 <1 cBN: 45; TiN: 30; TiB₂: 5; AlN: 5; 0.9 impurities such as W and Co: 14.1 C ≦8 <1 cBN: 45; TiN: 30; TiB₂: 5; AlN: 5; 1.0 impurities such as W and Co: 14 D ≦8 <1 cBN: 45; TiN: 30; TiB₂: 5; AlN: 5; 4.0 impurities such as W and Co: 11 E ≦8 <1 cBN: 45; TiN: 30; TiB₂: 5; AlN: 5; 9.0 impurities such as W and Co: 6 F ≦8 <1 cBN: 45; TiN: 30; TiB₂: 5; AlN: 5; 10   impurities such as W and Co: 5 G ≦8 1-1.5 cBN: 45; TiN: 30; TiB₂: 5; AlN: 5; 4.0 impurities such as W and Co: 11

TABLE 2 Details of Al₂O₃ coating method Gas introduced Step 1 Step 2 CO₂ (%) — 5 AlCl₃ (%) — 5 CO (%) — — H₂S (%) — 0.1 HCl (%) — 5 H₂ (%) 100  74.9 Pressure (Torr) 80 80 Temperature (° C.) 920  920 Processing time (min) 10 1,000

TABLE 3 Details of Al₂O₃ coating method Gas introduced Step 1 Step 2 Step 3 CO₂ (%) 5 5 5 AlCl₃ (%) — 5 5 CO (%) 2.5 2.5 — H₂S (%) — — 0.1 HCl (%) — 0.8 5 H₂ (%) 92.5 86.7 74.9 Pressure (Torr) 80 80 80 Temperature (° C.) 920 920 920 Processing time (min) 10 30 1,000

The Al₂O₃-coated sintered materials thus obtained were then each analyzed by electron microscope (SEM: scanning electron microscope) and EDS (energy-disperse X-ray spectroscopy). As a result, the Al₂O₃ layer was found to have a thickness of 25 μm and contain Al₂O₃particles having an average particle diameter (S) of 4.5 μm.

The cutting tools made of Al₂O₃-coated cBN-based sintered material thus prepared were then each precisely examined for the conditions of face and flank taking part in cutting by XRD (X-ray diffraction). As a result, κ-Al₂O₃ was found to have been formed under Condition 1 set forth in Table 2. Under Condition 2 set forth in Table 3, α-Al₂O₃which is oriented on (012) plane with an orientation index TC(012) of 1.1 was found to have been formed. The orientation index was determined by the previously described equation.

Subsequently, these inserts were each evaluated for cutting properties. Referring to the cutting conditions, the material to be cut was a round rod according to SUJ2 with a hardness HRC 65 having a V-shaped groove at two points along the longitudinal periphery thereof. The cutting speed was 150 m/min. The depth of cut was 0.2 mm. The feed rate was 0.1 mm/rev. The cutting was effected in a dry process. For the evaluation of cutting properties, a stereomicroscope and a surface profile measuring instrument were used to measure flank wear width and crater wear depth and observe how the insert had been worn. For comparison, a commercially available cBN-based sintered material for cutting hardened steel free of Al₂O₃ coating layer was similarly evaluated. The results are set forth in Table

TABLE 4 Cutting properties of Al₂O₃-coated cBN-based sintered material cBN-based Flank wear Crater wear sintered width during depth during material Coating 1 km cutting 1 km cutting No. substrate conditions (μm) (μm) Life against tool failure  1 A Condition 2 — — Al₂O₃ layer peeled at 0.5 km  2 A Interlayer + — — Al₂O₃ layer peeled at 0.6 km Condition 2  3 B Condition 2 41 12 Al₂O₃ layer peeled at 1.5 km  4 B Interlayer + 40 12 Al₂O₃ layer peeled at 1.4 km Condition 2  5 C Condition 2 40 11 Broken together with substrate at 5 km  6 C Interlayer + 40 12 Broken together with Condition 2 substrate at 5 km  7 D Condition 2 38 11 Broken together with substrate at 8 km  8 D Condition 1 58 13 Broken together with substrate at 4 km  9 E Condition 2 42 12 Broken together with substrate at 7 km 10 F Condition 2 59 12 Broken together with substrate at 3 km 11 G Condition 2 41 12 Al₂O₃ layer peeled at 1.2 km  12* D Not coated 60 22 Broken at 3 km  13* Commercially available 61 27 Broken at 3 km cBN-based sintered material tool for cutting hardened steel *Comparative Example

Summarizing Table 4, the following results were obtained.

If the substrate is free of Al₂O₃ or the content of Al₂O₃ falls below 1% by volume (Nos. 1-4), the adhesion of the coating layer is insufficient and a remarkable improvement of tool life cannot be observed. On the contrary, even if the content of Al₂O₃ is not less than 10% by volume (No. 10), the resulting improvement is insufficient. If the content of Al₂O₃ falls below 1.0% by volume, it causes uneven nucleation during coating, exerting an insufficient effect. On the contrary, if the content of Al₂O₃ is not less than 10%, the mechanical properties inherent to Al₂O₃ is presumably reflected in the mechanical properties of cBN-based sintered material, drastically deteriorating the breakage resistance of cBN-based sintered material substrate.

On the other hand, as can be seen in the results of Nos. 5, 6, 7 and 9, the incorporation of a proper amount of Al₂O₃ in a cBN-based sintered material substrate makes it possible to increase the adhesion of the Al₂O₃ layer or interlayer made of TiCxNyOz having an excellent bonding strength with Al₂O₃, enhancing the cutting properties. The reason why the adhesion of the Al₂O₃ layer or interlayer can be thus increased is presumably as follows:

(1) Al₂O₃ constituting the coating layer and TiCxNyOz undergo nucleation with Al₂O₃ contained in cBN-based sintered material substrate as a starting point; and

(2) the incorporation of Al₂O₃ in cBN-based sintered material substrate causes the residual stress characteristic to cBN-based sintered material substrate to change, relaxing misfit of coating layer to residual stress (thermal stress, internal stress).

If the particle diameter of Al₂O₃ particles in the substrate exceeds 1 μm (No. 11), the adhesion of Al₂O₃ coating layer is insufficient. This is because the homogeneous incorporation of finely divided Al₂O₃ particles having a particle diameter of not more than 1 μm in cBN-based sintered material substrate makes it possible to accelerate the formation of fine homogeneous nuclei during the formation of Al₂O₃ or TiC_(x)N_(y)O_(Z) layer and hence form an Al₂O₃ layer having an excellent crystallinity and adhesion.

As can be seen in the comparison of Nos. 7 and 8, the Al₂O₃ layer is preferably mainly composed of α-Al₂O₃. The coating of cBN-based sintered material substrate with α-Al₂O₃ with a good adhesion makes it possible to inhibit wear on relieve face and crater wear and hence drastically prolong the life of tool. The coating of cBN-based sintered material substrate with κ-Al₂O₃ with a good adhesion, too, makes it possible to inhibit crater wear and prolong the life of tool. However, wear on relieve face can be little inhibited.

EXAMPLE 2

cBN-based sintered material substrates containing cBN particles having an average particle diameter of not more than 2 μm and Al₂O₃ particles having an average particle diameter of less than 1 μm incorporated therein were each coated with TiCN and TiN by an ordinary CVD method, and then coated with Al₂O₃ by the same CVD method as in Example 1. During this procedure, the disposition of the cBN-based sintered material, the film-forming temperature, the carrier gas concentration, etc. were adjusted. In this manner, various cutting tools made Al₂O₃-coated cBN-based sintered material set forth in Tables 5, 6 and 7 were prepared.

These cutting tools made of Al₂O₃-coated cBN-based sintered material were then each precisely examined for the conditions of face and flank taking part in cutting by XRD. As a result, it was found that an α-Al₂O₃ coating layer having TC (hkl) of not less than 0.9 had been formed. TC(hkl) is the maximum orientation index of (hkl) plane among (012), (104), (110), (113), (024) and (116) planes.

TABLE 5 Composition of cBN- Constitution of based sintered material coating layer *1 No. (vol-%) (μm) TC(hkl) *2 S *2 1 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer: 30 TC(012) 4.5 0.9; TiB₂: 5; AlN: 5; 2 impurities 2 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer: 30 TC(012) 4.5 1.0; TiB₂: 5; AlN: 5; 2 impurities 3 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer/TiC_(0.5)N_(0.5) TC(012) 2.5 1.0; TiB₂: 5; AlN: 5; columnar crystal 2 impurities inhibition layer/ Al₂O₃ layer: 14/2/14 4 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer: 30; TC(012) 4.5 1.0; TiB₂: 5; AlN: 5; TiN0.5 surface layer 2 impurities 5 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer: 30; TC(012) 4.5 3.0; TiB₂: 5; AlN: 5; TiN0.5 surface layer 2 impurities 6 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer: 30 TC(012) 4.5 4.5; TiB₂: 5; AlN: 5; 2 impurities 7 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer: 30 TC(012) 4.5 5.5; TiB₂: 5; AlN: 5; 2 impurities 8 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer: 30 TC(012) 4.5 9.5; TiB₂: 5; AlN: 5; 2 impurities 9 cBN: 55; TiN: 24; a-Al₂O₃; Al₂O₃ layer: 30 TC(012) 4.5 10.5; TiB₂: 5; AlN: 5; 2 impurities *1 Texture coefficient of α-Al₂O₃ *2 Average crystal particle diameter of α-Al₂O₃

TABLE 6 Composition of cBN- Constitution of based sintered material coating layer *1 No. (vol-%) (μm) TC(hkl) *2 S *2 10 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer: 52 TC(012) 4.5 4.5; TiB₂: 5; AlN: 5; 2   impurities 11 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer: 50 TC(012) 4.5 4.5; TiB₂: 5; AlN: 5; TiC_(0.5)N_(0.5) 2   impurities interlayer: 1 12 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer: 55 TC(012) 4.5 4.5; TiB₂: 5; AlN: 5; TiC_(0.5)N_(0.5) 2   impurities interlayer: 1 13 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer: 50; TC(012) 10   4.5; TiB₂: 5; AlN: 5; TiC_(0.5)N_(0.5) 2   impurities interlayer: 1 14 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer: 50; TC(012) 12   4.5; TiB₂: 5; AlN: 5; TiC_(0.5)N_(0.5) 2   impurities interlayer: 1 15 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer: 30 TC(012) 3.0 4.5; TiB₂: 5; AlN: 5; 0.9 impurities 16 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer: 30 TC(012) 3.0 4.5; TiB₂: 5; AlN: 5; 1.0 impurities 17 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer: 30 TC(012) 3.0 4.5; TiB₂: 5; AlN: 5; 2   impurities 18 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer: 30 TC(012) 3.0 4.5; TiB₂: 5; AlN: 5; 2.5 impurities *1 Texture coefficient of α-Al₂O₃ *2 Average crystal particle diameter of α-Al₂O₃

TABLE 7 Composition of cBN- Constitution of based sintered material coating layer *1 No. (vol-%) (μm) TC(hkl) *2 S *2 19 cBN: 20; TiN: 60; α-Al₂O₃; Al₂O₃ layer: 30 TC(012) 4.5 4.5; TiB₂: 5; AlN: 5; 2 impurities 20 cBN: 18; TiN: 60; α-Al₂O₃; Al₂O₃ layer: 30; TC(012) 4.5 4.5; TiB₂: 5; AlN: 5; TiC_(0.5)N_(0.5) 2 impurities interlayer: 1 21 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer: 30 TC(012) 4.5 4.5; TiB₂: 5; AlN: 5; TiC_(0.5)N_(0.5) 2 impurities interlayer: 1 22 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer: 30; TC(012) 4.5 4.5; TiB₂: 5; AlN: 5; TiC_(0.5)N_(0.5) 2 impurities interlayer: 1 23 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer: 30; TC(012) 4.5 4.5; TiB₂: 5; AlN: 5; TiC_(0.5)N_(0.5) 2 impurities interlayer: 1: 24 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer: 30 TC(012) 4.5 4.5; TiB₂: 5; AlN: 5; 2 impurities 25 cBN: 55; TiN: 25; α-Al₂O₃; Al₂O₃ layer: 30 TC(012) 4.5 4.5; TiB₂: 5; AlN: 5; 2 impurities 26 Uncoated cBN sintered material/cBN: 55; TiN: 25; α-Al₂O₃: 4.5 TiB₂: 5; AlN: 5; impurities 27 Comparative: commercially available Al₂O₃-coated cemented carbide for cutting steel 28 Comparative: commercially available TiCN-coated thermet for cutting steel *1 Texture coefficient of α-Al₂O₃ *2 Average crystal particle diameter of α-Al₂O₃

Subsequently, these inserts were each evaluated for cutting properties. Referring to the cutting conditions, the material to be cut was a round rod according to SMC435 with a hardness HRC of 20 having a V-shaped groove at two points along the longitudinal periphery thereof. The cutting speed was 600 m/min. The depth of cutting was 0.5 mm. The feed rate was 0.5 mm/rev. The cutting was effected in a dry process. For the evaluation of cutting properties, a stereomicroscope and a surface profile measuring instrument were used to measure wear and observe how the insert had been worn. For comparison, a commercially available sintered material for cutting hardened steel free of Al₂O₃ coating layer was similarly evaluated. The results are set forth in Tables 8 and 9.

TABLE 8 Results of evaluation of cutting properties of various cutting tools made of Al₂O₃-coated cBN-based sintered material Flank wear width Crater wear depth during 1 km cutting during 1 km cutting Form of wear No. (μm) (μm) during 1 km cutting Tool life  1 — — — Coating layer peeled and broken at 0.5 km  2 140 7 Slightly chipped Lost together with substrate at 5.5 km  3 140 7 Smooth Broken together with substrate at 7 km  4 140 7 Slightly chipped Broken together with substrate at 5.5 km  5 140 7 Slightly chipped Broken together with substrate at 7 km  6 140 7 Slightly chipped Broken together with substrate at 7 km  7 140 7 Slightly chipped Broken together with substrate at 6 km  8 145 7 Slightly chipped Broken together with substrate at 5.5 km  9 145 7 Slightly chipped Broken together with substrate at 1.5 km 10 — — — Peeled during film forming 11 140 8 Slightly chipped Broken together with substrate at 6.5 km 12 140 12  Slightly chipped Coating layer broken at 1.5 km 13 140 7 Slightly chipped Broken together with substrate at 5.5 km 14 140 7 Drastically Coating layer broken at chipped 1.8 km

TABLE 9 Results of evaluation of cutting properties of various cutting tools made of Al₂O₃-coated cBN-based sintered material Flank wear Crater width wear depth during 1 km during 1 km Form of cutting cutting wear during No. (μm) (μm) 1 km cutting Tool life 15 205 17 Slightly chipped Cutting not allowed due to excessive wear at 2 km 16 150 9 Slightly chipped Broken together with substrate at 5.5 km 17 130 6 Smooth Broken together with substrate at 7.5 km 18 125 5 Smooth Broken together with substrate at 8 km 19 140 7 Slightly chipped Broken together with substrate at 4.5 km 20 142 8 Slightly chipped Broken together with substrate at 3.0 km 21 138 7 Slightly chipped Broken together with substrate at 7 km 22 139 6 Slightly chipped Broken together with substrate at 7 km 23 141 7 Slightly chipped Broken together with substrate at 7 km 24 142 7 Slightly chipped Broken together with substrate at 7 km 25 139 7 Slightly chipped Broken together with substrate at 7 km 26 210 21 Smooth Cutting not allowed due to excessive wear at 2 km 27 — — — Substrate plastically deformed to cause peeling and breakage of coating layer at 1.4 km 28 250 — Siightly chipped Cutting not allowed due to excessive wear at 1.5 km

As compared with the conventional cBN-based sintered material tool, coated cBN-based sintered material tool, coated cemented carbide tool for cutting steel and TiCN-coated thermet, the examples of the present invention made of an α-Al₂O₃ coating layer having TC(hkl) of not less than 1.0, TC(hkl) indicating the maximum orientation index of (hkl) plane among (012), (104), (110), (113), (024) and (116) planes, show a drastic improvement of flank wear resistance and crater wear resistance.

The reason why the examples of the present invention show a drastic improvement of flank wear resistance and crater wear resistance is presumably as follows:

α-Al₂O₃ is more excellent in mechanical properties such as hardness and toughness on (012), (104), (110), (113), (024) and (116) planes than on other crystal faces; and

Al₂O₃ grows as a columnar crystal. By allowing the columnar crystal to undergo orientation growth rather than random growth, the introduction of defects due to mechanical interference between crystalline particles can be inhibited, drastically enhancing the toughness of the coating layer.

On the other hand, the cutting tool of No. 15 having an orientation index TC(012) of 0.9 exhibits a deteriorated wear resistance, showing no improvement of tool life.

When the thickness of the Al₂O₃ layer, if provided alone, exceeds 50 μm (no. 10), the cutting tool is liable to cracking or peeling, showing a drastic deterioration of cutting properties. On the other hand, the provision of a TiC_(x)N_(y)O_(Z) layer as an interlayer on the interface of the cBN-based sintered material substrate with the Al₂O₃ coating layer makes it possible to inhibit the occurrence of cracking or peeling at the Al₂O₃ coating layer (no. 10). This is presumably because misfit of cBN-based sintered material substrate to the residual stress of the coating layer is relaxed by the TiC_(x)N_(y)O_(Z) layer as an interlayer. However, even if the foregoing interlayer is interposed between the layers, when the thickness of the Al₂O₃ layer exceeds 50 μm (No. 12), the resulting cutting properties are drastically deteriorated similarly.

As in Example 1, the homogeneous incorporation of fine Al₂O₃ particles having a particle diameter of not more than 1 μm in cBN-based sintered material substrate makes it possible to accelerate the formation of fine homogeneous nuclei during the formation of Al₂O₃ or TiC_(x)N_(y)O_(Z) layer and hence form an Al₂O₃ layer having an excellent crystallinity and adhesion. The thickness of all the Al₂O₃ coating layers are defined to be not less than 25 μm . It can be presumed from Nos. 5 and 17 that if the average crystal particle diameter (s) of α-Al₂O₃ particles constituting the α-Al₂O₃ coating layer is great under these conditions, the resulting product exhibits a deteriorated toughness. It can also be presumed from Nos. 13 and 14 that if the thickness of the α-Al₂O₃ coating layer is not more than 50 μm, when the average crystal particle diameter (s) of α-Al₂O₃ layer exceeds 10 μm , the α-Al₂O₃ coating layer can be remarkably broken.

The comparison of Nos. 1 to 9 shows that if the content of Al₂O₃ falls below 1.0% by volume, it causes uneven nucleation sparsely scattered during the formation of coating layer. Thus, the content of Al₂O₃ needs to be not less than 1.0% by volume. In particular, if the content of Al₂O₃ is not less than 3%, the resulting cutting tool exhibits an excellent adhesion. On the contrary, if the content of Al₂O₃ exceeds 5% by volume, the density of nuclei thus formed is too great, causing the introduction of defects into the crystal due to mutual mechanical interference during the growth of Al₂O₃ or TiC_(x)N_(y)O_(Z) and hence deteriorating the toughness of the coating layer. In particular, if the content of Al₂O₃ exceeds 10%, the mechanical properties inherent to Al₂O₃ is presumably reflected in the mechanical properties of cBN-based sintered material, drastically deteriorating the breakage resistance of cBN-based sintered material substrate. Accordingly, the content of Al₂O₃ in the cBN-based sintered material substrate is preferably from not less than 1.0% by volume to less than 10% by volume, more preferably from not less than 3% by volume to less than 5% by volume.

If the content of cBN in the cBN-based sintered material substrate falls below 20% by volume (No. 20), the resulting effect of cBN, which is inherently excellent in mechanical properties such as hardness and toughness, is presumably lessened, drastically deteriorating the breakage resistance of the cBN-based sintered material substrate.

The Al₂O₃-coated tool according to the present invention, even if coated with a single α-A₂O₃ layer, exhibits a better toughness than the conventional Al₂O₃-coated tools. In particular, the α-Al₂O₃ coating layer of No. 3 provided as a columnar crystal inhibition layer between Al₂O₃ layers has fine columnar crystal particles homogeneously oriented and thus exhibits an excellent toughness. Accordingly, the α-Al₂O₃ coating layer of No. 3 presumably can be smoothly worn without slightly chipping itself and shows a prolonged life against loss as compared with other α-Al₂O₃ coating layers.

EXAMPLE 3

cBN-based sintered material substrates made of cBN particles having an average particle diameter of not more than 5 μm and Al₂O₃ particles having an average particle diameter of less than 1 μm incorporated therein were each coated with Al₂O₃ by the same CVD method as in Example 1. During this procedure, the disposition of the cBN-based sintered material, the film-forming temperature, the carrier gas concentration, etc. were adjusted. In this manner, various cutting tools made of Al₂O₃-coated cBN-based sintered material set forth in Table 10 were prepared.

These cutting tools made of Al₂O₃-coated cBN-based sintered material were then each precisely examined for the conditions of face and flank taking part in cutting by XRD. As a result, it was found that an α-Al₂O₃ coating layer having TC hkl) of not less than 0.9 had been formed. TC(hkl) is the maximum orientation index of (hkl) plane among (012), (104), (110), (113), (024) and (116) planes.

TABLE 10 Composition of cBN-based Constitution of No. sintered material (vol-%) coating layer *1 (μm) TC (hkl) *2 S *2 1 cBN: 55; TiN: 25; α-Al₂O₃; 4.5; Al₂O₃ layer: 4 TC(012) 1.8 0.5 TiB₂: 5; AlN: 5; impurities 2 cBN: 55; TiN: 25; α-Al₂O₃; 4.5; Al₂O₃ layer: 4 TC(104) 1.8 0.5 TiB₂: 5; AlN: 5; impurities 3 cBN: 55; TiN: 25; α-Al₂O₃; 4.5; Al₂O₃ layer: 4 TC(116) 1.8 0.5 TiB₂: 5; AlN 5; impurities 4 cBN: 55; TIN: 25 α-Al₂O₃; 4.5; Al₂O₃ layer: 4 TC(110) 1.8 0.5 TiB₂: 5; AlN 5; impurities 5 cBN: 55; TiN: 25 α-Al₂O₃; 4.5; Al₂O₃ layer: 4 TC(113) 1.8 0.5 TiB₂: 5; AlN 5; impurities 6 cBN: 55; TiN: 25 α-Al₂O₃; 4.5; Al₂O₃ layer: 4 TC(024) 1.8 0.5 TiB₂: 5; AlN 5; impurities 7 cBN: 55; TiN: 25, α-Al₂O₃; 4.5; Al₂O₃ layer: 4 TC(104) 0.9 0.5 TiB₂: 5; AlN: 5; impurities 8 cBN: 55; TiN: 25; α-Al₂O₃; 4.5; Al₂O_(3 l)ayer: 4 TC(104) 1.1 0.5 TiB₂: 5; AlN: 5; impurities *1: Texture coefficient of α-Al₂O₃ *2: Average crystal particle diameter of α-Al₂O₃

TABLE 11 Formulation of cBN-based Constitution of No. sintered material (vol-%) coating layer *1 (μm) TC (hkl) *2 S *2  9 cBN: 55; TiN: 25; α-Al₂O₂; 4.5; Al₂O₃ layer: 4 TC(104) 2.3 0.5 TiB₂: 5; AlN: 5; impurities 10 cBN: 55; TiN: 25;α-Al₂O₃; 4.5; Al₂O₂ layer: 7 TC(104) 1.8 0.5 TiB₂: 5; AlN: 5; impurities 11 cBN: 55; TiN: 25; α-Al₂O₃; 4.5; Al₂O₃ layer: 25 TC(104) 1.8 0.5 TiB₂: 5; AlN: 5; impurities 12 cBN: 55; TiN: 25; α-Al₂O₂; 4.5; Al₂O₃ layer: 25 TC(104) 1.8 4.0 TiB₂: 5; AlN: 5; impurities 13 cBN: 55; TiN: 25; α-Al₂O₃; 4.5; Al₂O₂ layer: 25 TC(104) 1.8 4.5 TiB₂: 5; AIN: 5; impurities 14 Uncoated cBN sintered material/cBN: 55; TiN: 25; α-Al₂O₃: 4.5; TiB₂: 5; AlN: 5; impurities 15 Comparative: commercially available Al₂O₃-coated cemented carbide for cutting steel 16 Comparative: commercially available Al₂O₂-TiC-based ceramics for cutting steel *1: Texture coefficient of α-Al₂O₃ *2: Average crystal particle diameter of α-Al₂O₃

Subsequently, these tips were each evaluated for cutting properties. The cutting conditions were the same as used in Example 2. In some detail, the material to be cut was a round rod according to SMC435 with a hardness HRC of 20 having a V-shaped groove at two points along the longitudinal periphery thereof. The cutting speed was 600 m/min. The depth of cut was 0.5 mm. The feed rate was 0.5 mm/rev. The cutting was effected in a dry process. For the evaluation of cutting properties, a stereomicroscope and a surface profile measuring instrument were used to measure wear and observe how the insert had been worn. For comparison, a commercially available sintered material for cutting hardened steel free of Al₂O₃ coating layer was similarly evaluated. The results are set forth in Table 12.

TABLE 12 Results of evaluation of cutting properties of various cutting tools made of Al₂O₃-coated cBN-based sintered material Flank wear Crater width wear depth Form during 1 during of wear km cutting 1 km cut- during 1 No. (μm) ting (μm) km cutting Tool life 1 110 15 Smooth Broken together with substrate at 4.5 km 2 110 15 Smooth Broken together with substrate at 4.5 ks 3 110 14 Smooth Broken together with substrate at 4.5 km 4 110 13 Smooth Broken together with substrate at 4.5 km 5 110 14 Smooth Broken together with substrate at 4.5 km 6 100 14 Smooth Broken together with substrate at 4.5 km 7 200 17 Slightly chipped Cutting not allowed due to excessive flank wear at 2.5 km 8 120 15 Smooth Broken together with substrate at 4 km 9 100 15 Smooth Broken together with substrate at 5 km 10 100 11 Smooth Broken together with substrate at 5 km 11 100 7 Smooth Broken together with substrate at 5 km 12 120 8 Smooth Broken together with substrate at 5.5 km 13 145 7 Slightly chipped Broken together with substrate at 4.5 km 14 210 20 Smooth Cutting not allowed due to excessive wear at 1.9 km 15 — — — Substrate plastically deformed to cause peeling and loss at 1.3 km 16 — — Slightly chipped Heavily broken at 0.1 km

The results in Table 12 gave the following discoveries. The comparison of Nos. 11 to 13 shows that as the average crystal particle diameter of α-Al₂O₃ particles constituting the α-Al₂O₃ coating layer increases, the wear resistance and the smoothness of the worn surf ace are deteriorated. This is presumably attributed to the low toughness of coarse-grained α-Al₂O₃. If the thickness of the α-Al₂O₃ coating layer is not more than 25 μm, when the average crystal particle diameter of α-Al₂O₃ particles exceeds 4 μm, the resulting product exhibits a drastically deteriorated wear resistance. The product of No. 7, which exhibits TC(104) of less than 1.0, exhibits an excessive flank wear and thus shows a reduced tool life.

As compared with Example 2, Example 3 exhibits an increased crater wear mainly attributed to thermal wear by the factor corresponding to the reduction of the thickness of the α-Al₂O₃ coating layer, which is excellent in thermal stability. However, Example 3 exhibits a reduction in flank wear mainly attributed to mechanical wear by the factor corresponding to the reduction of the average crystal particle diameter of the α-Al₂O₃ particles. Thus, the product of Example 3 shows a smoothly worn surface.

Accordingly, in cutting requiring high dimensional precision or high surface integrity, it is preferred that the thickness (d) of the α-Al₂O₃ coating layer be from 0.5 μm to 25 μm (0.5 μm≦d≦25 μm) and the average crystal particle diameter (s) of the α-Al₂O₃ particles be from 0.01 μm to 4 μm . If the life against tool failure is emphasized, it is preferred that the thickness (d) of the α-Al₂O₃ coating layer be from 25 μm to 50 μm (25 μm<d≦50 μm) and the average crystal particle diameter (s) of the α-Al₂O₃ particles be from 0.01 μm to 10 Mm.

As mentioned above, the present invention has the following effects:

(1) The incorporation of a proper amount of Al₂O₃ in the cBN-based sintered material substrate makes it possible to control the density of nuclei formed during the formation of Al₂O₃ coating layer and the crystallinity of the Al₂O₃ coating layer thus formed and hence produce an Al₂O₃coating layer having an excellent adhesion to the substrate and a good crystallinity.

(2) An Al₂O₃ coating layer oriented on (012), (104),(110),(113),(024) and (116) planes having an excellent wear resistance and strength can be formed on the surface of the tool to be abraded by the material to be cut.

(3) The coated sintered material having the foregoing effects (1) and (2) can provide a cutting tool which exhibits a prolonged life in cutting of iron-based high hardness difficultly-cuttable materials or high speed and efficiency cutting of steel, which can be effected over a reduced period of time or impossible with existing tools due to the rise in cutting temperature. 

What is claimed is:
 1. A cutting tool made of Al₂O₃-coated cBN-based sintered material comprising: cBN-based sintered material substrate; one or more Al₂O₃ layers coating said cBN-based sintered material on at least a part of a surface of said cBN-based sintered material substrate taking part in cutting; wherein said sintered material substrate comprises cBN in an amount of from 20% to 99% by volume and Al₂O₃ having an average crystalline particle diameter of not more than 1 μM in an amount of from not less than 1.0% to less than 10% by volume, said Al₂O₃ layer has a thickness (d) of from 0.5 μm to 50 μm, and the average crystalline particle diameter (s) of Al₂O₃ is from 0.01 μm to 4 μm if the thickness (d) of said Al₂O₃ layer is from 0.5 μm to 25 μm (0.5 μm≦d≦25 μm)or the average crystalline particle diameter (s) of Al₂O₃ is from 0.01 μm to 10 μm if the thickness (d) of said Al₂O₃ layer is from more than 25 μm to 50 μm (25 μm<d<50 μm).
 2. The cutting tool made of Al₂O₃-coated cBN-based sintered material according to claim 1, wherein said cBN sintered material substrate comprises Al₂O₃ in an amount of from not less than 3.0% to less than 5.0% by volume.
 3. The cutting tool made of Al₂O₃-coated cBN-based sintered material according to claim 1, wherein said Al₂O₃ layer comprises α-Al₂O₃ as a main component.
 4. The cutting tool made of Al₂O₃-coated cBN-based sintered material according to claim 1, wherein said Al₂O₃ layer comprises α-Al₂O₃ having an orientation index TC(012) of not less than 1.0, TC(104) of not less than 1.0, TC(110) of not less than 1.0, TC(113) of not less than 1.0, TC(024) of not less than 1.0 or TC(116) of not less than 1.0 and said orientation index is defined by the following equation: TC(hkl)=I(hkl)/Io(hkl)×[(l/n)Σ{(hkl)/Io(hkl)}]⁻¹ where I(hkl): Intensity of (hkl) diffraction ray in XRD; Io(hkl): Diffraction intensity in ASTM card of XRD; and n: Number of diffraction rays used in calculation ((hkl) diffraction rays used are (012),(104),(110),(113),(024) and (116).
 5. The cutting tool made of Al₂O₃-coated cBN-based sintered material according to claim 1, further comprising an interlayer made of TiC_(x)N_(y)O_(Z) provided at the interface of said Al₂O₃ with said cBN-based sintered material substrate.
 6. The cutting tool made of Al₂O₃-coated cBN-based sintered material according to claim 1, wherein a plurality of Al₂O₃ layers are provided, each of which are laminated with a TiC_(x)N_(y)O_(Z) layer interposed therebetween; and the total thickness of the plurality of Al₂O₃ layers is used as the thickness of said Al₂O₃ layer.
 7. The cutting tool made of Al₂O₃-coated cBN-based sintered material according to claim 1, wherein a TiC_(x)N_(y)O_(Z) layer is coated as an outermost layer thereof.
 8. The cutting tool made of Al₂O₃-coated cBN-based sintered material according to claim 1, wherein said cBN-based sintered material substrate comprises cBN and a binder phase, and said binder phase comprises at least one selected from the group consisting of nitride, carbide and boride of metals belonging to the groups 4a, 5a and 6a in the periodic table and mutual solid-solution thereof. 